Thermoelectric elements

ABSTRACT

Thermoelectric elements of both P-type and N-type lead tellurides having unique characteristics including, particularly in the case of the P-type, a figure-of-merit 90% above that of the best commercial P-type element, are produced by a new process involving as key steps chill casting, cold pressing and sintering to 85-90% theoretical density under protective atmosphere.

FIELD OF THE INVENTION

The present invention relates generally to the art of thermoelectricpower generation and is more particularly concerned with newthermoelectric elements having unique properties, and with a novelmethod for making those elements.

BACKGROUND OF THE INVENTION

Thermoelectric conversion has long been known and generally recognizedas affording the prospect of important advantages as a source ofelectric power, particularly in the form of lightweight, multi-fuelpower generators. It has also been known for decades that thesemiconducting compound lead telluride (PbTe) is the most efficientthermoelectric material for power generation in the temperature range ofmajor interest from 125°-550° C. The bright promise of this technologyin practical application has, however, never been realized. Thus, allthe efforts made heretofore to improve the efficiency of thermoelectricconversion elements have resulted in only a marginal gain in thatall-important quality as measured by the so-called "figure-of-merit Z",defined as:

    Z=S.sup.2 /pK

where S is the Seebeck coefficient, p is the electrical resistivity, andK is the thermal conductivity of the thermoelectric material.

SUMMARY OF THE INVENTION

On the basis of our discoveries set forth in detail below, it ispossible now for the first time to produce consistently thermoelectricelements having figures-of-merit up to 90% higher than those previouslyknown. Further, this amazing result is not obtained at the expense ofany other desirable property. Thus, mechanical strength, and thermal-and mechanical-shock resistance of the thermoelectric elements of thisinvention are comparable to the best of the prior art, and they arestable chemically, electrically, and metallurgically under conditions ofnormal use. They are also readily joined or attached with chemical andmetallurgical stability to low-resistance electrical contacts. In otherwords, unlike thermoelectric elements of the prior art which arecrack-prone, particularly in the region of contact, those of thisinvention retain their integrity throughout over protracted periods ofnormal use.

An important discovery of ours upon which this invention is predicatedconcerns the method by which thermoelectric elements are made.Specifically, we have found that by melting and chill casting athermoelectric composition, mechanically reducing the resulting ingot tofine powder, cold pressing the powder and sintering the resulting greenbody under protective atmosphere, an article having novel thermoelectricproperties can be produced. Thus, for example, using a P-typecomposition of the prior art, one practicing the process of thisinvention can produce a thermoelectric element far superior to thatresulting from the prior art practice involving relatively slow coolingthe casting and hot pressing the powder.

We have further suprisingly found that although the elements of thisinvention have about 85% to 87% theoretical density in contrast to thenear theoretical density typical of the hot-pressed bodies of the priorart, they have substantially lower electrical resistivity. They alsohave increased Seebeck coefficients, a correlation contradictory toprior knowledge and experience and without scientifically proven cause.These effects may be connected to the observed weight loss of 3-5%during the sintering process of this invention as this slight change inchemical composition results in a two-phase material. The majority phaseappears to be Pb(Te, Se) and the minority phase is elemental Pb. Theprecipitation of Pb may leach sodium from the Pb(Te, Se) phase,resulting in an increased Seebeck coefficient. While these speculationscannot be confirmed at this time, the two-phase nature of these newproducts and the fine grain size are readily observed by standardmicroscopic techniques.

Additional discoveries of ours include the fact that while sintering maybe accomplished in 20 to 25 hours at 700° to 800° C., for best resultsand especially for superior and unique thermoelectric properties, theP-type material should be sintered at 745°-755° C. for 21.5 to 22.5hours while the N-type material should be sintered at 715°-725° C. forthat same length of time. In addition, sintering should always becarried out under a protective atmosphere such as flowing nitrogen andpreferably the sintered bodies should be cooled to room temperatureunder similar protection of nitrogen or the like.

Briefly described, the method of this invention comprises the steps ofmelting a lead telluride thermoelectric composition, chill casting theresulting melt to produce a fine-grained ingot of substantially uniformcomposition throughout, mechanically reducing the ingot to provide apowder of particle size less than about 60-mesh, cold pressing thepowder to form a green body, and sintering the green body underprotective atmosphere.

Likewise broadly and generally stated, a thermoelectric element of thisinvention comprises an alloy of lead telluride having porosity i.e.density of about 85 to 87% theoretical density and microstructurecharacterized by about 2% of a filamentary second phase distributedsubstantially uniformly through the element and segregated in the grainboundaries. Such an element of the P-type comprises an alloy of between80 and 97 mol percent lead telluride between about 3 and 20 mol percentlead selenide and in addition containing between about 0.5 and 2.0atomic percent sodium, and said element further has an uniquely highthermoelectric figure-of-merit. The N-type analog is an element of alloycomposition between about 80 and 97 mol percent lead telluride andbetween about 3 and 20 mol percent germanium telluride and in additioncontains between about 0.01 and 0.2 mol percent lead iodide.

BRIEF DESCRIPTION OF THE DRAWINGS

In the drawings accompanying and forming a part of this specification,

FIG. 1 is a photomicrograph of a P-type thermoelectric element of thisinvention (magnification 7/16"=100 microns);

FIG. 2 is a photomicrograph of a N-type thermoelectric element of thisinvention (magnification 7/16"=100 microns);

FIG. 3 is a chart bearing three curves representing plots of Seebeckcoefficient versus temperature data gatheredt experimentally in one caseand derived from the literature in the others;

FIG. 4 is another chart like that of FIG. 3 in which the three curvesrepresent plots of electrical resistivity data versus temperature fromthe safe experimental and literature sources as those of FIG. 3;

FIG. 5 is still another chart like that of FIGS. 3 and 4 bearing curvesrepresenting plots of thermal conductivity versus temperature for thethree sources indicated immediately above;

FIG. 6 is another chart like those of FIGS. 3-5 bearing curvesrepresenting plots of figure-of-merit Z values versus temperature ofp-type thermoelectric materials derived from the data represented by theseveral curves of each of FIGS. 3-5; and,

FIG. 7 is a chart like that of FIG. 6 on which the same data plots havebeen made, the three curves, however, representing figures-of-merit Z ofN-type thermoelectric materials including one of this invention and twoof the prior art sources attributed in FIGS. 3-5.

DETAILED DESCRIPTION OF THE INVENTION

In practicing this invention in accordance with a preferred embodimentof it, a P-type thermoelectric element having the unique propertiesdescribed above is produced by a process which begins with the step ofcharging lead, tellurium, selenium and sodium dopant in requisiteamounts into a quartz crucible and introducing the crucible into aninduction heating coil in a vacuum casting furnace. When the charge hasbeen melted under an inert gas atmosphere, the alloy is cast into acarbon-coated, water-cooled, copper chill mold. The resulting somewhatfriable, fine-grained ingot of homogenous composition thus produced ispulverized and screened to fine powder which in the next step iscold-pressed to desired cylindrical green body size. The green body issintered by firing it under flowing nitrogen at 750° C. for 22 hours andthen furnace cooled under the same protective atmosphere to roomtemperature.

By carrying out the process in this manner, the detrimental effect ofingot inhomogeniety on the desirable thermoelectric properties of thealloy is avoided. Also, sintering in this manner results in a body whichis mechanically strong even though it is unusually porous.

In this case the amounts of alloy constituents PbTe and PbSe in molpercent are 95 and 5, respectively, but slight variations from theseamounts are possible and even desirable in certain situations andapplications and consequently contemplated in this preferred practice.

Melting in this case involves as a preliminary step the evacuation ofthe furnace and flushing of it several times with argon or helium toremove oxygen traces, then backfilling with the inert gas and heating to1,000° C. to melt down the charge and produce the thermoelectric alloy.

Since these melting and casting operations involve vaporization lossesof Te to the extent of approximately 0.8 weight percent of the totalcasting weight in spite of the blanket of one atmosphere of inert gas inthe furnace, that extra amount of Te is added to the casting charge inour preferred practice.

Pulverizing of the resulting ingot is easily accomplished because of thefriability and porosity of the body. The equipment used and particularlythe grinding mill or other means such as mortar and pestle, should becarefully cleaned to avoid contaminating the alloy. Thus, slightimpurities can have devastating effects upon the desired thermoelectricproperties of the ultimate product of this process.

The cold pressing operation is carried out with a cylindrical-cavity dieto provide a thermoelement green body about 2.5 cm long of 0.14 cmdiameter. Pressures from 30,000 to 70,000 lbs. per square inch aresuitable for this purpose, the latter being our preference.

As cold pressed, the thermoelectric element green bodies have inferiorthermoelectric and mechanical strength characteristics. Accordingly,sintering is necessary and is carried out in an inert or reducingatmosphere and results in establishment of equilibrium between theprimary PbTe phase and the minor excess phase. In accordance with ourpreference sintering is carried out under a nitrogen atmosphere inequipment selected and prepared to avoid contamination, the green bodiesbeing placed in quartz boats and carried thereby into the quartz tubesof the sintering furnace. Special care is taken to exclude oxygen fromthe sintering cycle because of its highly deleterious effects upon boththe electrical properties and the thermochemical stability of theultimate thermoelectric elements.

In another preferred embodiment of this invention, an N-typethermoelectric element of this invention is produced with the uniquecharacteristics described above by following basically the foregoingprocedure. In this case, of course, the requisite amounts of the severalconstituents necessary for the N-type thermoelectric properties are usedinstead of the constituents employed in P-type thermoelectric elementproduction. Those skilled in the art will also recognize that dependingupon the amounts of lead iodide (PbI₂) used, the ultimate thermoelementwill have various properties. Thus by using 0.055 mol percent of leadiodide as the dopant, the so-called "3N-type" is produced. When it isdesired to gain a different property, particularly figure-of-meritpeaking at a lower temperature, the "4N-type" is produced by using only0.01 mol percent of PbI₂. The practical significance of this differenceis that elements of the two materials may be segmented to obtain maximumthermoelectric efficiency over the temperature range of practicalimportance, i.e. 150°-560° C.

The melting and chill casting operations and the pulverizing and coldpressing operations in this instance are carried out in accordance withour preference as described in detail above in reference to theproduction of the P-type thermoelectric element. The sintering step,however, is carried out under substantially different temperatureconditions, that is at temperatures well below those stated in thepractice detailed immediately above. Desirably the sintering time is asstated above, that is about 21.5 to 22.5 hours but the temperature towhich the green body is subjected during firing is controlled within the715°-725° C. range. Exposure to temperatures between 700° and 800° forseveral hours is usually suitable for establishment of equilibrium inthe cold press material of either P-type or N-type but again, inaccordance with our preference, to obtain the best properties the firingtimes and temperatures are limited as stated just above and in thedetailed description of P-type element production.

Those skilled in the art will gain a further and better understanding ofthis invention and the new and important advantages which it affords,from the following illustrative, but not limiting, examples of thisinvention as it has been carried out in actual practice.

EXAMPLE I

In an experimental operation, a P-type thermoelectric element wasproduced and tested with the results set out below. At the outset, acharge consisting of pieces no larger than 3/4 inch in any dimension wasprepared as follows:

    ______________________________________                                        Material      Weight (grams)                                                  ______________________________________                                        Lead          623.394                                                         Tellurium     369.726                                                         Selenium      11.88                                                           Sodium        0.484                                                           Total         1005.484                                                        ______________________________________                                    

The sodium was placed in the bottom of a clean fused silica crucible andimmediately covered with selenium, lead and then tellurium and thecrucible is placed in a vacuum furnace chamber which was promptlyevacuated and then flushed three times with argon and backfilled withone atmosphere of argon. The crucible and contents were induction heatedto about 1,000° in about 15 minutes and the melted charge was then chillcast as it was poured into a graphite-coated, water-cooled, copper mold.By having the mold in the vacuum furnace chamber the melting and castingoperations were carried on under the same protective atmosphere and thethermoelectric alloy produced in the melting operation was not exposedto contact with the room atmosphere while the alloy was at elevatedtemperature.

The resulting friable, somewhat porous, alloy ingot upon removal fromthe mold was broken into pieces smaller than about 1/2in. by 1/2in. by 1in. using a mortar and pestle and those pieces were reduced to powder ina Straub grinding mill and screened, the -60 mesh +200 mesh fractionbeing selected for cold pressing as the next step of the process.

Using a steel die of suitable dimensions, a cylindrical green body wasproduced by charging the selected powder fraction into and filling thedie and applying a pressure of 60,000 psi to the charge. In thisinstance the resulting green body was 1 in. long and of diameter 0.346in.

Being mechanically comparatively weak and having inferior properties asa thermoelectric element, the green body was sintered to enhance itgreatly in both respects. This was done by first wrapping the body ingraphite tape, placing it in a fused silica boat and inserting the boatinto the mouth of a furnace tube through which a nitrogen atmosphere wasflowed continuously. After about 4 minutes the boat was moved into thefurnace hot zone and then after 22 hours at 750° C. the boat with itscharge was drawn back out to the furnace tube mouth. Finally, when theboat was cool enough to touch it was taken from the furnace tube and onreaching room temperature the thermoelectric element was removed,unwrapped and subjected to several tests. Data gathered in testing thisthermoelectric element are illustrated by Curves A, B and C of FIGS.3-5, respectively, which compare to Curves S, T and U representing anelement of the prior art and Curves W, X and Y representing anotherelement of the prior art. On visual examination no lamination, crack orother physical defect which might adversely affect its electrical ormechanical properties was observed. The density of the element was foundto be 85 percent of theoretical density of the material as indicated bythe photomicrograph of FIG. 1. The grain size of this elementapproximating 111 microns was much greater than that of a representativeprior art element (i.e. that of Curve S of FIG. 3) which approximated 37microns. Finally, in plotting the figure-of-merit which takes intoaccount all three of the properties represented by FIGS. 3-5 Curve D ofFIG. 6 was developed, illustrating the clear and very surprisingsuperiority of this element over thermoelectric elements of the typepreviously known in the art represented by Curves V and Z of FIG. 6.Indeed the breakthrough dimensions of this enhancement of desirableproperties attests to the unobviousness of the present thermoelectricelement as well as of the method by which it is made and those skilledin the art will realize that one following the instructions detailedjust above in regard to this particular experiment can expect toreproduce this spectacular result in making such thermoelectricelements.

EXAMPLE II

Following the procedure set forth in detail in Example I, an N-typethermoelectric element was prepared and tested as described below. Inthis instance the charge was again of 1,000-grams size and consisted ofthe following:

    ______________________________________                                        Material      Weight (grams)                                                  ______________________________________                                        Lead          610.0                                                           Tellurium     378.95                                                          Germanium     11.05                                                           Lead Iodide   0.7728                                                          Total         1000.7728                                                       ______________________________________                                    

Departures from the procedural details set out in Example I mainlyconcern the necessity for using clean tools and containers throughout.Thus the same mortar and pestle, for example, were not used for both theP-type material of Example I and this N-type material. The melting andchill casting operations were as defined in detail in Example I and thecold pressing operation and sintering operation were also the sameexcept that in firing the thermoelectric element in this instance, thetemperature in the furnace hot zone was maintained at 720° C. instead of750° C.

Visual examination of the N-type thermoelectric element did not revealany lamination crack or other physical defect which might adverselyaffect its electrical or mechanical properties. Density of this body,however, was found to be slightly greater than the P-type body ofExample I being measured at 8.00 grams per cubic centimeter, indicatingdensity of about 87% theoretical which is confirmed by thephotomicrograph of FIG. 2.

The Seebeck coefficient, electrical resistivity and thermal conductivitymeasurements were made in this case as they were in the case of theP-type thermoelectric element of Example I. Thus thermal conductivity inboth instances was measured by the comparative method and the electricalresistivity and Seebeck coefficient measurements were all likewisemeasured by the same standard methods and means of the art. The dataresulting from these tests of this Example II product are consequentlyconsolidated in the manner described above in the figure-of-meritillustrated by Curve E of FIG. 7. In like manner Curves K and J of FIG.7 represent the figure-of-merit properties of N-type thermoelectricelements of the prior art.

Where amounts, percentages or proportions are stated in thisspecification and the appended claims, reference is to the weight basisunless otherwise expressly specified.

All sieve sizes recited herein and in the appended claims are U.S.Standard.

What is claimed is:
 1. A lead telluride thermoelectric element havingabout 85-87% theoretical density and microstructure characterized byabout 2% of a filamentary second phase distributed substantiallyuniformly and segregated in the grain boundaries, said element beingcrack free and having excellent thermal- and impact-shock resistance andbeing joinable to electric contacts without localized cracking.
 2. Athermoelectric element as described in claim 1 which is of the N-typecomprising an alloy of between about 80 and 97 mol percent PbTe andbetween about 3 and 20 mol percent GeTe and in addition contains betweenabout 0.01 and 0.2 mol percent PbI₂.
 3. A thermoelectric element ofclaim 2 in which the alloy contains about 95 mol percent PbTe and about5 mol percent GeTe and in addition contains about 0.055 mol percentPbI₂.
 4. A P-type thermoelectric element comprising an alloy of betweenabout 80 and 97 mol percent PbTe and between about 3 and 20 mol percentPbSe and additionally containing between about 0.5 and 2.0 atomicpercent sodium, said element having between about 85% and 87%theoretical density and microstructure characterized by 2% of afilamentary second phase distributed throughout the body and segregatedat the grain boundaries, and said element having a thermoelectricfigure-of-merit greater than about 0.0025 per degree C. over the rangeof temperature from about 200° C. to about 500° C.
 5. A thermoelectricelement as described in claim 4 in which the alloy contains about 95 molpercent PbTe and 5 mol percent PbSe and in addition contains about 1atomic percent sodium.
 6. A lead telluride thermoelectric element havingabout 85-87% theoretical density and microstructure characterized byabout 2% of a filamentary second phased distrubuted substantiallyuniformly and segregated in the grain boundaries.said element beingcrack free and having excellent thermo- and impact- shock resistant andbeing joinable to electric contacts without localizing cracking producedby the following steps of:(a) melting a PbTe thermoelectric composition,(b) chill casting the resulting melt to produce a fine-grained ingot ofsubstantially uniform composition throughout, (c) mechanically reducingthe ingot to provide powder of particle size less than about 60-mesh,(d) cold pressing the powder about 30,000 to 70,000 psi to form agenerally cylindrical green body, (e) sintering the green body at atemperature between 700° and 800° C. for 20 to 24 hours, and (f) finallycooling the resulting sintering body to room temperature under neutralatmosphere.